EP0064243A2 - Procédé de soudage d'éléments en alliage de titane avec l'application d'une pièce intercalaire en titane - Google Patents

Procédé de soudage d'éléments en alliage de titane avec l'application d'une pièce intercalaire en titane Download PDF

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Publication number
EP0064243A2
EP0064243A2 EP82103462A EP82103462A EP0064243A2 EP 0064243 A2 EP0064243 A2 EP 0064243A2 EP 82103462 A EP82103462 A EP 82103462A EP 82103462 A EP82103462 A EP 82103462A EP 0064243 A2 EP0064243 A2 EP 0064243A2
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EP
European Patent Office
Prior art keywords
welding
titanium alloy
alloy
heat treatment
titanium
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Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP82103462A
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German (de)
English (en)
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EP0064243A3 (en
EP0064243B1 (fr
Inventor
Tsuneo Kakimi
Megumi Nakanose
Hiroshi Satoh
Takaharu Konishi
Hisanao Kita
Takamitsu Nakazaki
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Hitachi Ltd
Nissan Motor Co Ltd
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Hitachi Ltd
Nissan Motor Co Ltd
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Publication date
Priority claimed from JP56065578A external-priority patent/JPS57181776A/ja
Priority claimed from JP56065577A external-priority patent/JPS57181775A/ja
Application filed by Hitachi Ltd, Nissan Motor Co Ltd filed Critical Hitachi Ltd
Publication of EP0064243A2 publication Critical patent/EP0064243A2/fr
Publication of EP0064243A3 publication Critical patent/EP0064243A3/en
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Publication of EP0064243B1 publication Critical patent/EP0064243B1/fr
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
    • B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/32—Selection of soldering or welding materials proper with the principal constituent melting at more than 1550 degrees C
    • B23K35/325—Ti as the principal constituent

Definitions

  • This invention relates to a method of welding parts of a titanium alloy fundamentally in the manner of butt welding.
  • Titanium is a relatively light metal with a specific gravity of 5.54 g/cm 3 . Because of a relatively high value of specific strength (strength/density) and excellence in heat resistance and corrosion resistance, the use of titanium has been increasing in the area of chemical processing equipment and also in many other areas. Moreover, the addition of certain alloying elements to titanium gives high strength titanium alloys that are very high in specific strength, corrosion resistance and heat resistance and suited to engineering material also in other properties. Accordingly the application of such titanium alloys has been broadening particularly in the aerospace industries. For example, titanium alloys are widely used in the skins of aircraft and the motor cases of rockets.
  • the weld metal section (a section brought to molten state during the welding process and solidified again) given by.this welding method is liable to become considerably lower in toughness than the base metal, and it is difficult to improve the mechanical properties of this weld metal section by a postwelding heat treatment and sometimes, depending on the type of the titanium alloy, the weld metal section becomes more brittle by heat treatment.
  • TIG arc welding process which is an inert-gas shielded-arc welding process using a nonconsumable tungsten electrode, by using a commercially pure titanium rod as filler metal.
  • TIG arc welding process which is an inert-gas shielded-arc welding process using a nonconsumable tungsten electrode
  • the present invention provides a method of welding opposite end surfaces of two titanium alloy parts kept in alignment by a high energy-density welding process, and the principal feature of the invention is to closely interpose an insert member between the end surfaces of the two titanium alloy parts, the material of the insert member consisting essentially of 0-3% by weight of aluminum and the balance of titanium.
  • the high energy-density welding process is performed so as to fuse the insert member as well as adjacent end surface regions of the two titanium alloy parts.
  • Electron beam welding, laser beam welding and TIG arc welding can be named as typical examples of high energy-density welding processes useful in the present invention.
  • the welding method according to the invention is applicable to both alpha type titanium alloys and alpha-beta type titanium alloys, and also to beta type titanium alloys.
  • the welding method according to the invention is applicable to every type of titanium alloys.
  • alpha type titanium alloys containing relatively large amounts of alpha-stabilizing elements such as aluminum and tin
  • suitable and commercially available alloys are Ti-5%Al-2.5%Sn, Ti-8%Al-1%Mo-1%V, Ti-5%Al-5%Sn-5%Zr and Ti-7%Al-12%Zr.
  • alpha-beta type titanium alloys containing at least one beta-stabilizing element such as vanadium, chromium or molybdenum in addition to an adequate amount of aluminum
  • Ti-6%Al-4%V and Ti-6%Al-6%V-2%Sn are named as suitable and commercially available examples.
  • beta type titanium alloys containing relatively large amounts of beta-stabilizing elements Ti-13%V-11%Cr-3%Al and Ti-15%Mo-5%Zr are named as commercially available examples.
  • the material of the insert member characteristic of the welding method according to the invention may be either practically pure titanium or a binary alloy consisting essentially of up to 3% by weight of aluminum and the balance of titanium.
  • titanium of Type 1, 2 or 3 according to JIS (Japanese Industrial Standard) H 4650 is useful as the insert material.
  • Titanium of this class may contain less than 0.20% (or 0.40%) of 0, less than 0.05% (or 0.07%) of N, less than 0.15% of H and less than 0.20% (or 0.25%, or 0.40%) of Fe.
  • a practically pure titanium insert member of this class can be produced from a titanium ingot obtained by melting sponge titanium either in vacuum or in an inert gas atmosphere in an electric arc furnace of the consumable electrode type or a plasma-beam furnace by a suitable shaping method such as forging, extrusion or rolling.
  • a titanium insert member is produced through a two-stage fusion process having the steps of producing a rod-shaped titanium ingot in a plasma-beam furnace, melting this ingot in vacuum by using the ingot as consumable electrode, and subjecting the ingot obtained through the second fusion step to a suitable shaping operation.
  • ELI extra low interstitial titanium
  • the contents of interstitial impurity elements are limited to the extent of less than 0.08% of 0, less than 0.01% (or 0.015%) of N and less than 0.02% (or 0.03%) of C.
  • the insert material By using a titanium alloy consisting essentially of up to 3.0% by weight of Al and the balance of Ti as the insert material, it is possible to further enhance the tensile strength and proof stress of the weld metal given by a method according to the invention.
  • the content of aluminum in the insert material is limited to 3.0% in order to ensure that the content of aluminum in the weld metal does not exceed about 6%, which is accepted as the upper limit of aluminum capable of existing in the state of solid solution, to thereby prevent the introduced aluminum from unfavorably affecting the elongation and toughness of the weld metal.
  • Two titanium alloy parts to be welded together are brought into alignment, and a suitably shaped insert member of pure titanium or titanium-aluminum alloy is closely interposed between oppositely positioned end surfaces of the two titanium alloy parts.
  • the titanium alloy parts to be welded may be either plates or bars or rods.
  • the insert member is usually in the form of plate or sheet. The resultant assemly of the base metal and the insert member is subjected to a high energy-density welding process.
  • practical examples of high energy-density welding processes are electron beam welding that utilizes a concentrated beam of electrons as the source of welding heat, laser beam welding that utilizes a laser light beam as the source of welding heat, plasma arc welding that utilizes a plasma arc as the source of welding heat, and TIG arc welding with a nonconsumable electrode such as tungsten electrode that utilizes an inert shield gas preferably containing helium and, preferably, is performed with application of a pulse current.
  • electron beam welding and laser beam welding processes are particularly advantageous because of the possibility of realizing higher energy density compared with arc welding processes, ease of controlling the welding heat and the possibility of enhancing the precision and efficiency of welding.
  • a primary advantage of a high energy-density welding process typified by electron beam welding resides in that the amount of energy required per unit length of the weld line is very small, so that both a fused zone and adjacent heat-affected zones in this welding process remain relaively small in width. Accordingly, in the weld joint given by this welding method the residual strains and stresses are very small and localized within a very narrow region, and therefore the weld joint exhibits good mechanical properties even in the state as welded followed by no heat treatment.
  • a high energy-density welding process has the effect of producing a molten pool which is under adequate agitation because there occurs a boiling phenomenon in a region irradiated by the beam or arc, whereby there occurs thorough alloying in the fused zone to the effect of preventing any portion of the insert material from remaining unalloyed in the resultant weld metal. This is another reason for good mechanical properties of a weld joint given by a method according to the invention.
  • both down hand welding by a vertical beam or arc and horizontal welding by a horizontal beam or arc are possible, and in both cases the welding may be performed in the manner of either piercing welding or nonpiercing welding (partial penetration welding).
  • piercing welding is performed by down hand welding, sometimes it will be difficult to support the molten pool (a region brought to molten state during welding) solely by the surface tension of the penetration bead on the reverse side, depending on the thickness of the titanium alloy parts in the weld zone. In such a case, it will be necessary to use a backing strip so as to produce a partial penetration state to thereby prevent the fall of the molten pool.
  • Horizontal welding is further classified roughly into upwardly travelling welding, downwardly travelling welding, laterally travelling welding and circumferentially travelling welding, and in the present invention a suitable method is chosen with due consideration of the shape and size of the parts to be welded and the welding conditions.
  • the swinging of the beam in the welding operation should be controlled in the rate of swinging, angles of swinging and the directions of swinging considering that these factors affect the degree of movement of the molten metal in the molten pool. Besides, it is desirable to adequately determine the degree of penetration of the beam and the beam current. In some cases, it is preferred to employ a locally vacuum welding method so as to maintain only a region in the vicinity of the weld line in vacuum.
  • TIG arc welding When performing the welding method according to the invention by TIG arc welding, it is preferred to perform the TIG arc welding with application of a pulse current because this is effective for further promotion of alloying in the fused zone during welding and, hence, improvement in the mechanical properties of the weld joint.
  • the welding method according to the invention gives an excellent weld joint when the volume of the insert member is within a suitable range. More particularly, it is preferred that the material of the insert member occupies 5 to 85% of unit volume of a molten metal section formed during the welding operation and, hence occupies 5 to 85% of unit volume of the weld metal section given by the welding.
  • Fig. 1 by way of example, when an insert sheet 14 having a thickness t i is interposed between edge faces of two pieces 10 and 12 of a titanium alloy plate having a thickness T and the welding is performed such that a resultant weld metal section 16 in Fig. 2 has a thickness t w , it is suitable that the proportion of the thickness t.
  • the thickness of the insert member 14 to the thickness t of the weld metal section 16, t i /t w ranges from 5 to 85% by percentage.
  • the proportion of the insert material is less than 5% by volume, the weld metal section is liable to become considerably lower in toughness than the base metal.
  • the proportion of the insert material exceeds 85% by volume, the thickness of the insert member will become greater than the width of the electron beam utilized in the welding operation and the agitation of the melted insert material will remain insufficient.
  • a selection can be made from stress and strain relief heat treatment, diffusion heat treatment and a combination of solid solution heat treatment and an aging treatment.
  • a stress and strain relief heat treatment it is suitable to heat the weld joint at a temperature in the range from about 450°C to about 950°C for about 15 min to about 15 hr, followed by either air cooling or water quenching.
  • a diffusion heat treatment it is suitable to heat the weld joint at a temperature above 800°C for about 15 min to about 15 hr, followed by either water quenching or air cooling.
  • solid solution heat treatment In the case of a combination of solid solution heat treatment and aging treatment, it is suitable to first perform a solid solution heat treatment consisting of heating at a temperature in the range from about 800 0 C to about 1000 0 C for about 15 min to about 6 hr and subsequent water quenching, oil quenching or air cooling and then perform an aging treatment consisting of heating at a temperature in the range from about 400°C to about 680°C for about 15 min to about 15 hr and subsequent air cooling. If desired the aging treatment may be carried out by repeating relatively short heating several times, and it is also optional to perform a heat treament including over aging.
  • alpha type titanium alloys have the hexagonal structure that is stable at lower temperatures and, hence, are hardly heat-treatable. Accordingly, the above described combination of solid solution heat treatment and the subsequent aging treatment is applicable to alpha-beta type titanium alloys and should be performed so as to appropriately adjust the fine-grain structure of the weld metal in connection with the alpha-to-beta and beta-to-alpha transformations of the employed alloy to thereby achieve improvement and stabilization of the mechanical properties of the weld joint.
  • the base metal was a Ti-6Al-4V alloy plate having a thickness T of 40 mm, and an ELI titanium sheet having a thickness t i of either 0.6 mm or 1.2 mm was employed as the insert material.
  • Tables 1 and 2 show the results of analysis of the titanium alloy plate and the titanium sheet, respectively.
  • two pieces 10 and 12 of the titanium alloy plate were subjected to butt welding by electron beam welding with the titanium sheet 14 closely inserted between the opposite edges of the two pieces 10 and 12 of the titanium alloy plate.
  • the 0.6 mm thick insert 14 and the 1.2 mm thick insert 14 were used individually and alternately.
  • the major surfaces of the assembled workpieces were set vertical, and the direction of the electron beam was made horizontal as indicated by arrow A in Fig. 1 and the electron beam was moved laterally as indicated by arrow B.
  • the electron beam welding equipment was operated so as to accomplish horizontal piercing welding under the following welding conditions.
  • test pieces for tensile strength test were cut out of the weld metal section 16 in the state as welded. These test pieces were in the shape as shown in Fig. 3 and all cut out along the weld line. The dimensions of each test piece were as follows.
  • the above described electron beam welding operation was performed without using any insert material, and the test pieces were cut out of the resultant weld metal section.
  • This example relates to a heat treatment subsequent to the electron beam welding operation of Example 1A. No modifications were made to the base metal, insert material, welding method and welding conditions described in Example 1A.
  • Example 1A From each of the three kinds of welded bodies obtained respectively by using the 0.6 mm thick insert, 1.2 mm thick insert and no insert, a sample in the shape of a rectangular plate 12.5 mm in width, 300 mm in length and 5 mm in thickness was cut out with the weld metal section 16 in the middle of the sample plate.
  • Each sample plate was subjected first to a solid solution heat treatment consisting of heating at 933°C for 30 min and subsequent water quenching and next to an aging treatment consisting of heating at 545 0 C for 6 hr and subsequent air cooling. After the heat treatment the test pieces shown in Fig. 3 and described in Example 1A were cut out of the respective sample plates and subjected to the tensile strength test. Table 5 shows the results of the test. For comparison, the data obtained in Example 1A without the heat treatment are parenthesized in.Table 5.
  • Example 1B had the effect of considerably enhancing the strength of the weld metal section with some descrease in the elongation. Also it can be seen that the use of the titanium insert in the butt welding resulted in noticeable improvement in the toughness of the weld metal section after the heat treatment.
  • This example too relates to a heat treament subsequent to the welding operation of Example 1A.
  • Example 1A Using the 40 mm thick titanium alloy plate and the 0.6 mm thick titanium sheet described in Example 1A, the electron beam welding operation of Example 1A was performed by the same method under the same conditions. Then, a sample in the shape of the rectangular plate mentioned in Example 1B was cut out of the welded body with the weld metal section in the middle of the sample plate, and the sample plate was subjected to a diffusion treatment consisting of heating at 948 0 C for 10 hr and subsequent water quenching. After that, the distribution of chemical composition of the weld metal section in the sample plate was analyzed by means of X-ray microanalyser at equal intervals in the direction of the thickness t w in Fig. 2. The result of the analysis is presented in Table 6.
  • the base metal was the 40 mm thick plate of the Ti-6Al-4V alloy described in Example 1A, and a Ti-1.5A1 alloy sheet having a thickness t i of either 0.6 mm or 1.2 mm was employed as the insert material.
  • Table 7 shows the result of analysis of the Ti-1.5Al alloy sheet.
  • Example 1A the electron beam welding operation described in Example 1A was performed with no modifications to the wedling method and welding conditions. For reference, the same welding operation was performed without using any insert material.
  • the test pieces shown in Fig. 3 and described in Example 1A were cut of the weld metal section 16 of every welded body (as-welded) obtained in this example and subjected to the tensile test to examine the mechanical properties of the weld metal section in the direction of the weld line. The results of the test are shown in Table 8.
  • the data in Table 8 show that the change in the insert material from practically pure titanium to the titanium-aluminum alloy produced some increase in the strength of the weld metal section 16 accompanied by some decrease in the elongation.
  • This example relates to a heat treatment subsequent to the electron beam welding operation of Examle 2A. No modifications were made to the base metal, insert material, welding method and welding conditions described in Example 2A. From each of the three kinds of welded bodies obtained respectively by using the 0.6 mm thick insert, 1.2 mm thick insert and no insert, a sample in the shape of the rectangular plate described in Example 1B was cut out with the weld metal section 16 in the middle of the sample plate. In accordance with Example 1B, each sample sample plate was subjected first to the solid solution heat treatment (heating at 933 0 C for 30 min and subsequent water quenching) and, next to the aging treatment (heating at 545°C for 6 hr and subsequent air cooling).
  • Example 10 shows the results of the test.
  • Table 10 shows the results of the test.
  • the data obtained in Example 2A without the heat treatment are parenthesized in Table 10.
  • Example 2B had the effect of considerably enhancing the strength of the weld metal section with some decrease in the elongation. Also it can be seen that the use of the titanium-aluminum alloy insert in the butt welding resulted in noticeable improvement in the toughness of the weld metal section after the heat treatment.
  • a 2.5 mm thick plate of Ti-6Al-4V alloy of the composition shown in Table 1 was employed as the base metal, and a 0.5 mm thick sheet of ELI titanium of the composition shown in Table 2 was used as the insert material.
  • the titanium sheet 14 was inserted between the opposite edges of two pieces 10 and 12 of the titanium alloy plate.
  • This assembly was subjected to TIG arc welding with application of a pulse current under the following welding conditions.
  • the welding operation was performed such that the thickness t w of the weld metal section 16 in Fig. 2 became 5.5 mm.
  • the test pieces shown in Fig. 3 were cut out of the weld metal section 16 of the welded body (as-welded) along the direction of the weld line and subjected to the tensile test.
  • the data obtained in this test indicated that the welded metal was satisfactory in both strength and toughness.
  • the distribution of chemical composition of the weld metal section 16 was analyzed by means of X-ray microanalyser at equal intervals in the direction of the thickness t w in Fig. 2. From the result of the analysis the weld metal section was confirmed to have a thoroughly dispersed and alloyed structure.
  • This example relates to a heat treatment subsequent to the pulsed TIG arc welding operation of Example 3A. No modifications were made to the base metal, insert material, welding method and welding conditions described in Example 3A.
  • the welded body was subjected first to a solid solution heat treatment consisting of heating in a vacuum furnace maintained at 933 0 C for 20 min and subsequent oil quenching and next to an aging treatment consisting of heating at 545°C for 5 hr and subsequent air cooling.
  • a solid solution heat treatment consisting of heating in a vacuum furnace maintained at 933 0 C for 20 min and subsequent oil quenching and next to an aging treatment consisting of heating at 545°C for 5 hr and subsequent air cooling.
  • the mechanical properties of the weld metal section 16 and the distribution of chemical composition in the direction of the thickness t of the weld metal section were examined in accordance w with Example 3A. Also in this example, it was confirmed that the weld metal section was satisfactory in both strength and toughness and had a thoroughly dispersed and alloyed structure.

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EP82103462A 1981-04-30 1982-04-23 Procédé de soudage d'éléments en alliage de titane avec l'application d'une pièce intercalaire en titane Expired EP0064243B1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP56065578A JPS57181776A (en) 1981-04-30 1981-04-30 Joining method for titanium alloy
JP56065577A JPS57181775A (en) 1981-04-30 1981-04-30 Welding method for titanium alloy
JP65577/81 1981-04-30
JP65578/81 1981-04-30

Related Child Applications (2)

Application Number Title Priority Date Filing Date
EP85102484A Division EP0163018A3 (fr) 1981-04-30 1982-04-23 Procédé de soudage d'éléments en alliage de titane avec l'application d'une pièce intercalaire constituée essentiellement de 0 à 3 % en poids d'aluminium et pour le reste de titane
EP85102484.4 Division-Into 1985-03-05

Publications (3)

Publication Number Publication Date
EP0064243A2 true EP0064243A2 (fr) 1982-11-10
EP0064243A3 EP0064243A3 (en) 1983-01-26
EP0064243B1 EP0064243B1 (fr) 1986-09-17

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EP85102484A Withdrawn EP0163018A3 (fr) 1981-04-30 1982-04-23 Procédé de soudage d'éléments en alliage de titane avec l'application d'une pièce intercalaire constituée essentiellement de 0 à 3 % en poids d'aluminium et pour le reste de titane
EP82103462A Expired EP0064243B1 (fr) 1981-04-30 1982-04-23 Procédé de soudage d'éléments en alliage de titane avec l'application d'une pièce intercalaire en titane

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EP85102484A Withdrawn EP0163018A3 (fr) 1981-04-30 1982-04-23 Procédé de soudage d'éléments en alliage de titane avec l'application d'une pièce intercalaire constituée essentiellement de 0 à 3 % en poids d'aluminium et pour le reste de titane

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US (1) US4503314A (fr)
EP (2) EP0163018A3 (fr)
DE (1) DE3273284D1 (fr)

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CN114309910B (zh) * 2021-12-31 2023-04-07 浙江工业大学 一种铜铬锆合金的电子束焊接工艺及焊后热处理方法
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EP0064243A3 (en) 1983-01-26
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EP0163018A2 (fr) 1985-12-04
EP0163018A3 (fr) 1988-02-10
EP0064243B1 (fr) 1986-09-17

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